Journal of Stress AnalysisVol. 3, No. 1, Spring − Summer 2018

An Experimental Investigation into Wear Resistance ofMg-SiC Nanocomposite Produced at High Rate of Com-paction

G.H. Majzoobia,∗, K. Rahmania, A. AtrianbaMechanical Engineering Department, Bu-Ali Sina University, Hamedan, Iran.bMechanical Engineering Department, Najafabad Branch, Islamic Azad University, Najafabad, Iran.

Article info

Article history:Received 27 April 2018Received in revised form19 September 2018Accepted 20 September 2018

Keywords:SiCNanocompositePowder metallurgyDynamic compactionWear

Abstract

The Mg-SiC nanocomposite specimens were produced at low strain rate of8×10−3s−1 using a universal INSTRON testing machine, strain rate of about8×102s−1 using a drop hammer and at strain rate of about 1.6×103s−1employing a Split Hopkinson Pressure Bar (SHPB). Tribological behaviorof the samples was investigated in this work. The compaction process wasperformed at the temperature of 723K. The results showed increase in the wearresistance as the nano reinforcement increased. The results also indicated thatas the reinforcement content increased to 10 vol%, the weight loss reducedapproximately by 63%, 58%, and 35% for the samples fabricated by SHPB,drop hammer, and quasi-static hot pressing, respectively. The results alsosuggested that the wear rate of samples fabricated by SHPB was nearly 40%lower than that for quasi-statically fabricated samples and non-reinforcedsamples.

1. Introduction

Particulates reinforced Mg matrix composites (MMCs)have increasingly found application in aerospace andautomotive industries. Concurrent demands on highwear resistance and weight reduction in automotive in-dustries have motivated researchers to perform variousstudies on MMCs [1-7]. The literature suggests thatthe wear resistance and strength of Mg and its alloyscan be enhanced by reinforcing them with ceramic par-ticles, such as Al2O3, SiC, MgO, TiC, B4C, TiB2, andZnO [8].

In most powder metallurgy (PM) techniques, thecompaction is performed quasi-statically whereas insome cases the compaction is carried out at high rateof loading. Hot pressing [9], hot isostatic pressing[10], and mechanical milling, and hot extrusion [11, 12]

are typical examples of techniques in which the com-paction loads are applied quasi-statically. High rateof compactions [13, 14] are accomplished through dy-namic loading or shock wave loadings [15]. In lat-ter techniques, some devices like dropping hammeror explosive-compressed gas accelerated projectile areused for compaction. The main advantage of high rateconsolidation methods is that hot sintering is primar-ily not necessary for compaction. In exchange, the im-pact energy usually supplies the high local tempera-ture rise at the powder particle interfaces which is ad-equate for local metallurgical bonding. Therefore, dur-ing dynamic compaction, the microstructural changeslike grain coarsening and particles aggregation can beminimized [16].

Several researchers such as Thakur et al. [17]and Francis et al. [18] have studied quasi-static com-

∗Corresponding author: G.H. Majzoobi (Professor)E-mail address: gh_majzoobi@basu.ac.irhttp://dx.doi.org/10.22084/jrstan.2018.16240.1048ISSN: 2588-2597

35

paction. Jiang et al. [19] investigated the feasibilityof the fabrication of B4C particulates reinforced Mgby powder metallurgy (PM) technique. Wang et al.[20] and Yan et al. [21] also applied impact energy forcompaction of powder materials. Faruqui et al. [22]produced Mg-SiC composites using mechanical millingand underwater shock consolidation. Atrian et al. [23]presented a comparative study on dynamic compactionand quasi-static hot pressing for fabrication of Al7075-SiC nanocomposite. Majzoobi et al. [24] also producedAl7075-B4C composite by some techniques with vari-ous densification rates [23, 25].

There are several studies on the effects of SiC par-ticles on the wear properties of Mg and its alloys. Forexample, Lim et al. [3] reported slight improvementin the wear resistance of AZ91 alloy reinforced with8 vol% SiC (particle size of 14µm) under the load of10N. Thakur and Dhindaw [2] also obtained that well-dispersed SiC particles may lead to higher wear resis-tance and lower friction coefficient (FC) in Al and Mgmetals. Similar results were also presented by Lim etal. [3]. Further improvement of tribological propertiesencouraged some researchers to incorporate nano rein-forcements into pure Mg [4, 5]. Mondal and Kumar [26]observed decreased wear rate of AE42 Mg alloy hybridcomposites reinforced with Saffil short fibers and SiCparticles in comparison to the Saffilnshort fibers rein-forced composite and unreinforced alloy. Umeda et al.[7] showed that carbon nanotubes (CNTs) and SiO2reinforcements could improve the wear tolerance anddecrease the friction coefficient (FC) of hybrid com-posites. Majzoobi et al. [27] also studied the tribologi-cal properties and the wear mechanisms of dynamicallycompacted Al7075-SiC nanocomposite. In the currentinvestigation, Mg-SiC nanocomposite was produced athigh rate of loading using a SHPB and a drop hammerand at low rate of loading using an Instron univer-sal testing machine. The main objective in this workwas to explore the tribological properties and the wearmechanisms in the samples produced at various rate ofloading.

2. Experiments

2.1. Materials and Fabrication of Samples

In this study, Mg powder with purity of 99.5% withparticle size of 100�m (regular morphology) was usedas matrix and SiC powder with purity of 99% and par-ticle size of 75nm (spherical morphology) was used asreinforcing phase. Further information can be foundin [13] and [14]. The specimens were produced usingthe SHPB and drop hammer (DH) described in thereferences [13] and [14], respectively. In order to inves-tigate the effects of nanoparticle content, cylindricalnanocomposite samples (with diameter of 15mm andlength of 11-12mm) with 0, 1.5, 3, 5 and 10% volumefraction of SiC were produced at the temperatures of

723K. The procedure of producing the samples can befound in [27] and [28].

2.2. Quasi-static Hot Pressing

Nanocomposite powder was hot pressed quasi-statically using an INSTRON universal testing ma-chine. In order to have a proper compaction, it wasrequired to calculate the optimum duration and thelevel of the pressure necessary to obtain the maximumdensity [23]. To do this, eight pure Mg specimens wereproduced at 723K and under the pressures of 300 and600MPa for 5, 15, 25, and 35min time duration.

Fig. 1 illustrates the effect of pressure level andtime duration on the density. As the figure suggests,the pressure of 600MPa gives the higher density andconsequently, this pressure and its corresponding timeduration (25min) were selected to produce the puresamples with 0-10 vol% SiC content.

Fig. 1. Density-time histories for two compact pres-sure.

Therefore, the compaction tests were carried outat the rate of 5mm/min that corresponds to a strainrate of around 8.0×10−3s−1. To prevent from forma-tion of void and pore, the pressure was released whentemperature dropped below 573K [23].

2.3. Dynamic Compaction Using Drop Ham-mer

A mechanical drop hammer [14] was used for dynamiccompaction of nanocomposite powders. The schematicview of the device is depicted in Fig. 2a. In thisdevice, a 60kg weight is dropped from the height of3.5m and hits the specimen at an impact velocity ofaround 8m/s (based on v =

√2gh equation). This

impact speed corresponds to a strain rate of around0.8×10−3s−1. The dropping hammer delivers around2kJ energy (E = Mv2/2) to the powder for com-paction. As mentioned earlier, the compaction wasperformed at the temperature of 723K. Further detailscan be found in [14].

An Experimental Investigation into Wear Resistance of Mg-SiC Nanocomposite Produced at High Rate ofCompaction: 35–45 36

Fig. 2. The schematic views of (a) The drop hammer and (b) The die.

The schematic view of the die is shown in Fig.2b. The die and the punch were made of Mo40(1.7225) and VCN150 (1.6582) steel, respectively to re-sist against thermal and impacting loads. Two tablets(5mm length) of VCN150 steel were also mounted ontop and beneath of powder to reduce the spring-backand to preserve the surface quality of the compact

The required temperature (maximum about 450◦C)was supplied by a 1200W furnace. The impact on thepowder was accomplished when the powder temper-ature reached a steady state. After compaction, thesamples were ejected out of the die and were cooled atambient temperature.

2.4. High Rate Compaction Utilizing SHPB

The high rate compactions were carried out utilizing aSHPB set up. Fig. 3 schematically depicts a SHPB,which consists of three bars; striker, incident (input),and transmitter (output). The input and output barsin the current research had a diameter of 40mm, lengthof 3m, and were made of a high strength steel alloy(Maraging steel) with an ultimate strength of about1600MPa. In this set-up, mechanically milled Mg-SiCpowder was poured in a die which had been mountedbetween the input and output bars of the SHPB. Theset up geometry, its components and the compactionprocedure are fully described in [13]. The compactiontemperature was 723K for all experiments. The reasonis explained in [13].

2.5. Characterizing Tests

To evaluate the effects of processing techniques, as wellas the SiC reinforcement content on the samples hard-ness, the Vickers microhardness of compacted sam-

ples was measured. For microhardness measurement,a 100gf for 15s was applied to the specimen using atetragonal indenter [29].

Fig. 3. The schematic view of the Split Hopkinsonset-up with loading tool.

Dry sliding wear tests were performed utilizing apin-on-disc test device shown in Fig. 4 according toASTM G99 [30]. A pin-on-disc instrument was usedto evaluate the wear loss as well as the friction coef-ficient. To this end, the compacted specimens with15mm diameter were placed in a 30mm diameter disk-shape container. Before each test, the pin and samplesurface were cleaned with acetone. All the tests weredone on various applied loads of 10 and 20N with slid-ing speeds of 0.09m/s. To have a deeper insight intothe matter, the wear tests were performed for two vari-ous sliding distances of 250 and 500m. After each test,the specimen and pin were cleaned with organic sol-vents to remove traces. The sample was weighted (ac-curacy of 0.1mg) before and after testing to determinethe amount of wear loss.

Journal of Stress Analysis/ Vol. 3, No. 1/ Spring − Summer 2018 37

Fig. 4. Pin-on-disk wear mechanism.

3. Results and Discussion

3.1. Microhardeness

Variation of Vickers microhardness of fabricated spec-imens versus different amounts of SiC vol% for differ-ent compaction techniques is illustrated in Figure 5.As the figure implies, 10 vol% SiC reinforcement hasincreased the microhardness of the compacted samplesfabricated using SHPB, drop hammer, and quasi-staticpressing by around 45%, 32% and 28 %, respectively.Nano reinforcement enhances the hardness mainly dueto its hardening effects and its intrinsic hardness [31].Seetharama et al. [32], Jiang et al. [33] and Umedaet al. [7] also reported similar observations in theirinvestigations. Higher micro-hardness of samples fab-ricated by SHPB was attributed to more severe workhardening and stronger bonding [34].

3.2. Wear Properties

3.2.1. Sliding Distance Effects

Variation of weight loss versus sliding distance undersliding speed of 0.09m/s and normal load of 20N isshown in Figure 6 for two various sliding distances of250 and 500m. As it is observed, weight loss increaseswith increasing the sliding distance. The figure alsoshows the highest wear resistance for the samples fab-ricated using SHPB. It is also seen in the figure that theweight loss decreases as the reinforcement content in-creases. The weight loss of the compacted samples bySHPB decreases from about 1.17 to 0.43mg/m (63%

reduction) when the SiC content increases from 0 to10 vol%. The high wear resistance of Mg-SiC samplesproduced by SHPB can be attributed to its increasedhardness and also to the strong bonding between thenanoreinforcement and Mg matrix that facilitates theload transfer from the matrix to the hard particles [22,34]. This confirms the results provided by Wang etal. [35] and Selvam et al. [36]. Similar increase inthe wear resistance of the nanocomposite samples fab-ricated by drop hammer and quasi-static hot pressingfor the increased nano reinforcement content can be ob-served. It is believed that this improvement is directlyassociated with the increase of hardness and strengthof the nanocomposites with reinforcement level. Theconnection between hardness and wear loss can be ex-plained by Archard’s law which describes an inverseproportionality between hardness and the wear rate ofa material [37]. The results show that variations of mi-crohardness versus weight loss confirms the Archard’sequation. Shanthi et al. [38] and Lim et al. [3] alsoreported similar findings.

Fig. 5. Variation of microhardness of the top surfacevs SiC content.

3.3. Load Effects

Normal interfacial loads in contacting components playa vital role in wear and erosion mechanisms in indus-try. Therefore, the study of the effects of normal loadson tribological behavior of materials is a requirement[4]. Variation of weight loss versus load at sliding speedof 0.09m/s and different normal loads is shown in Fig.7. As the figure shows, weight loss increases with theincrease of normal load from 10 to 20N for all methods.It is also evident from Fig. 7d that the weight loss ofall specimens enhances with the increase in load. Thehighest rate for the increase is obtained for the quasistatic compaction and the lowest rate is obtained forSHPB implying that the rate of weight loss decreaseswith the increase of strain rate. The increase of weightloss with the increase of the normal load can be at-tributed to the increased plastic deformation [39]. Fur-

An Experimental Investigation into Wear Resistance of Mg-SiC Nanocomposite Produced at High Rate ofCompaction: 35–45 38

thermore, the addition of SiC nanoparticles to Mg ma-trix decreases the weight loss due to strong bonding be-tween Mg and SiC particles during consolidation [36].Considering the applied load of 20N, the reduction ofweight loss, as the reinforcement content increases to10 vol%, is around 63%, 58%, and 35% for the samplesfabricated by SHPB, drop hammer, and quasi-statichot pressing, respectively.

Having weight loss for a specific sliding distance,one can simply calculate the wear rate as the ratio ofweight loss to sliding distance. Variation of wear rateversus the SiC nano particles content is typically illus-trated in Fig. 8 for the sliding distance of 500m and20N normal load. As the figure indicates, wear ratedecreases with increasing nano reinforcement. In ad-dition, compaction with higher densification rates hasled to lower wear rates. For example, the wear ratefor samples fabricated by SHPB is nearly 40% lowerthan that for quasi-statically fabricated samples with-out reinforcement. For Mg-10 vol% SiC samples the

reduction of wear rate for SHPB is about 70%. Similarresults were reported by Yao et al. [40] for wear resis-tance of AZ91/TiC composite reinforced with TiC andLim et al. [3] for AZ91 alloy reinforced with SiC.

3.4. Worn Surface Analysis

As stated before, nano reinforcement could remarkablyimprove the wear resistance of the samples. In or-der to investigate this finding more precisely, the wornsurfaces were examined using SEM micrographs withEDS analysis. SEM pictures of the worn surfaces ofthe specimens produced by the high rate compactionmethods employed in this work are depicted in Figs. 9to 11. It is obvious in the figures that as the reinforcingcontent increases, the wear track becomes smaller andthe grooves width decreases . Moreover, the grooveson the samples fabricated by SHPB are narrower andshallower compared with drop hammer and quasi-staticcompacted samples. These observations are indicationsof adhesive friction mechanism [41].

Fig. 6. Variation of weight loss for the applied load of 20N against sliding distance for samples fabricated by(a) SHPB, (b) Drop hammer, (c) Uniaxial quasi-static pressing, (d) A comparative view.

Journal of Stress Analysis/ Vol. 3, No. 1/ Spring − Summer 2018 39

Fig. 7. Variation of wear loss versus the applied load at the sliding distance of 500m for the samples fabricatedby: (a) SHPB, (b) Drop hammer, (c) Quasi-static hot pressing, (d) a comparative view.

Fig. 8. The effect of SiC vol% on the wear rate underthe applied load of 20N and sliding distance of 500mfor different fabrication techniques.

A comparison between parts (a) to (c) of each fig-ure (Figs. 9-11) reveals that the quasi-statically com-pacted samples have more craters and delaminationson their surfaces. These observations imply that thesamples fabricated by SHPB have more strength andhardness as well as stronger bonding between Mg andSiC particles [13] and [14].

Actually, for the samples with lower microhardnessthe counter faces between the pin and the sample sur-face increase, therefore more materials are detachedfrom the sample’s surface. This detachment may bedue to adhesive friction that consequently increases thewear rate. Lower wear rate in the samples fabricatedby SHPB is traced back to the mild wear with abra-sive wear mechanism and shows improved condition forwear behavior [36]. Additionally, nano reinforcementsdecreased the FC and plastic deformation, thereforethey have altered the severe adhesive wear mechanismto the mild abrasive wear (see the continuous and par-allel grooves in SHPB samples) [42]. Abrasive wear isdue to movement of the high-hardness pin over the low-hardness material, which makes some grooves propa-gating to the sample surface. Following grooves cre-ation, the material begins to flow, some delaminationhappens and craters are produced [43]. Higher sur-face hardness due to nano reinforcement or obtainedby higher compaction velocity (fabrication by SHPB,drop hammer and quasi-static hot pressing) reducesadhesion features and converts the wear mechanism toabrasive.

An Experimental Investigation into Wear Resistance of Mg-SiC Nanocomposite Produced at High Rate ofCompaction: 35–45 40

Fig. 9. SEM micrograph of wear track of Mg-0 vol% SiC compacted samples by: (a) SHPB, (b) Drop hammer,(c) Quasi-static hot pressing.

Fig. 10. SEM micrograph of wear track of Mg-5 vol% SiC compacted samples by: (a) SHPB, (b) Drop hammer,(c) Quasi-static hot pressing.

Fig. 11. SEM micrograph of wear track of Mg-10 vol% SiC compacted samples by: (a) SHPB, (b) Drophammer, (c) Quasi-static hot pressing.

Fig. 12. Wear track of Mg-5% SiC sample fabricated by SHPB for different magnifications.

Fig. 12 shows typical worn surface of a sample (Mg-5 vol% SiC) fabricated by SHPB at different magnifi-cations. Evidences of delamination and deep crater aswell as narrow grooves can be seen in Fig. 12 whichshows that abrasion and delamination are dominantwear mechanisms in the worn surfaces [27].

Fig. 13 shows the worn debris of samples fabri-cated by SHPB. As the figure suggests the size of weardebris is reduced when the reinforcing content is in-creased. As illustrated in part (a) of Figs. 9-11, in theworn surface of Mg-0 vol% SiC more separated anddeeper grooves are observed than for Mg-5 vol% SiC

and Mg-10 vol% SiC. These features along with plasticdeformation indicate adhesive and delamination wearmechanisms [41] in the worn surfaces. Furthermore,the morphology of the worn debris in Fig. 13 a demon-strates adhesive wear mechanism in Mg-0 vol% SiCsample. As mentioned earlier, nanocomposite sampleshad shallower grooves than Mg-0 vol% SiC which is dueto SiC reinforcing particles which enhance the samplehardness. The SiC inclusions also prohibit direct con-tact of the pin with Mg surface, therefore it reducesthe size and population of the worn debris [43].

Journal of Stress Analysis/ Vol. 3, No. 1/ Spring − Summer 2018 41

Fig. 13. SEM micrographs of worn debris of samples dynamically compacted by SHPB; (a) Mg, (b) Mg-5 vol%SiC, (c) Mg-10 vol% SiC.

The debris of smaller size are the result of abra-sive effect of hard nanoparticles and as a result, highernanoparticle fraction will cause more and smaller de-bris (See Figs. 13b and 13c). Therefore, it may be ar-gued that in the nanocomposites having smaller weardebris, compared with the monolithic material, the ef-fect of abrasive mechanism is more profound [9]. EDSpoint analysis of the worn debris seen in Fig. 13c ispresented in Fig. 14. The figure clearly shows very lowFe and Ti contents in the worn debris. The transfer ofFe and Ti from the steel pin to the worn surface is aclear indication that abrasion is one of the dominantwear mechanisms in wear test of samples.

Fig. 14. EDS point analysis of worn debris depictedin Fig. 13c.

3.5. Friction Coefficient

Variation of friction coefficient (FC) versus methodsand content reinforcement is presented in Figs. 15 and16. FC was measured by wear test under the normalload of 20N and the sliding speed of 0.09m/s. Fig. 15shows the variation of FC for Mg-5 vol% SiC nanocom-posites fabricated by different techniques. The severefluctuations of FC is due to aggregation or removal ofworn debris during the test [43]. According to Fig.15, the FC of Mg-5% SiC nanocomposite samples hasdecreased from about 0.27 to 0.15 when the produc-tion method alters from quasi-static to SHPB. Thelower FC for SHPB sample is believed to be due tostrong bonding between Mg and SiC nano particles,

hardness effects of SiC, and lower tendency to adhesivefriction during wear. In general, harder surfaces causesmaller contact area between the pin and the samplesurface, consequently, it gives rise to reduction of FC[9]. Umeda et al. [7] and Mohammad-Sharifi et al. [44]also reported similar observations in their investiga-tions. Variation of friction coefficient for nanocompos-ite samples fabricated by SHPB and under the appliedload of 20N for various SiC volume fractions is shownin Fig. 16. As the figure suggests, the average of FC isreduced significantly (around 81%) as the reinforcingcontent increases from 0 vol% to 10 vol%.

Fig. 15. Variation of friction coefficient of Mg-5 vol%SiC nanocomposites fabricated by different techniquesand under applied load of 20N and distance of 500m.

As Fig. 5 demonstrates, 10 vol% SiC nano re-inforcement has increased the microhardness signifi-cantly (about 45%) which in turn enhances the re-sistance against plastic deformation of surface layers.Hence, this behavior impedes adhesion of these plas-tically deformed layers to the surface [43]. Lower FCand wear rate of Mg-10 vol% SiC can also be explainedby Archard equation [37]. The largest variation of FCis seen for both the Mg-0 vol% SiC and Mg-5 vol%SiC; the reason is adhesion of wear debris to the sur-face that increases the surface roughness of the spec-imens. Moreover, the total wear loss is proportionalto the coefficient of friction [42]. It means that boththe uniform distribution of SiC hard nanoparticles andstrong bonding are effective in improving the tribo-

An Experimental Investigation into Wear Resistance of Mg-SiC Nanocomposite Produced at High Rate ofCompaction: 35–45 42

logical properties of the Mg-SiC nanocomposite by de-creasing the FC and wear loss during sliding [45, 46].Similar to this research, Jafari et al. [42] reported thatthe average of FC for nanostructured Al2024 sample ismuch smaller than Al2024-O and Al2024-T6 samplesmainly because of the high hardness of the nanostruc-tured alloy. Shanthi et al. [38] also reported similarobservations.

Fig. 16. Variation of friction coefficient for nanocom-posite samples fabricated by SHPB and under the ap-plied load of 20N and distance of 500m.

4. Conclusions

Based on the investigations presented in this paper,following concluding remarks may be drawn:

1. Incorporation of 10 vol% SiC reinforcement toMg matrix improved the Vickers microhard-ness by about 45% for SHPB method, 32% fordrop hammer method, and 24% for quasi_staticmethod.

2. Nano reinforcement could increase the wear resis-tances of the samples fabricated by quasi-staticand dynamic compaction procedures under thenormal load of 20N and sliding speed of 0.09m/s.The reduction of weight loss as the reinforce-ment content increased to 10 vol%, which is near63%, 58%, and 35% for the samples fabricated bySHPB, drop hammer, and quasi-static hot press-ing, respectively.

3. The wear rate of samples fabricated by SHPB wasnearly 40% lower than that for quasi-staticallyfabricated samples and non-reinforced samples,while it was about 70% for Mg-10 vol% SiC sam-ples.

4. SEM observations showed that the samples fab-ricated by SHPB had higher resistance againstsurfaces erosions such as scratches and wear.

5. The SEM analysis of the worn surfaces of thespecimens showed that the adhesion, abrasive,and delamination were the dominant wear mech-anisms.

References

[1] S. Sharma, B. Anand, M. Krishna, Evaluationof sliding wear behaviour of feldspar particle-reinforced magnesium alloy composites, Wear,241(1) (2000) 33-40.

[2] S.K. Thakur, B.K. Dhindaw, The influence of in-terfacial characteristics between SiC p and Mg/Almetal matrix on wear, coefficient of friction and mi-crohardness, Wear, 247(2) (2001) 191-201.

[3] C. Lim, S. Lim, M. Gupta, Wear behaviour of SiCp-reinforced magnesium matrix composites, Wear,255(1-6) (2003) 629-637.

[4] A. Atrian, G. Majzoobi, H. Bakhtiari, The Effectof Pre-compaction on Dynamic Compaction Pro-cess of Al/SiC Nanocomposite Powder, The Bi-Annual International Conference on Experimen-tal Solid Mechanics and Dynamics (X-Mech-2014),Tehran (2014).

[5] M. Habibnejad-Korayem, R. Mahmudi, Tribologi-cal behavior of pure Mg and AZ31 magnesium al-loy strengthened by Al2O3 nano-particles, Wear,268(3-4) (2010) 405-412.

[6] A. Mondal, S. Kumar, Dry sliding wear behaviourof magnesium alloy based hybrid composites intransverse direction, Mater. Sci. Forum, (783-786)(2014) 1530-1535.

[7] J. Umeda, K. Kondoh, H. Imai, Friction and wearbehavior of sintered magnesium composite rein-forced with CNT-Mg2Si/MgO, Mater. Sci. Eng. A.,504(1-2) (2009) 157-162.

[8] A. Mandal, B. Murty, M. Chakraborty, Wear be-haviour of near eutectic Al–Si alloy reinforced within-situ TiB2 particles, Mater. Sci. Eng. A., 506(1-2)(2009) 27-33.

[9] M., Jafari, M., M.H. Abbasi, M.H. Enayati, F.Karimzadeh, Mechanical properties of nanostruc-tured Al2024–MWCNT composite prepared by op-timized mechanical milling and hot pressing meth-ods, Adv. Powder. Technol., 23(2) (2012) 205-210.

[10] A. Ahmed, A. Neely, K. Shankar, T. Eddowes,Synthesis, tensile testing, and microstructuralcharacterization of nanometric SiC particulate-reinforced Al 7075 matrix composites, Metall.Mater. Trans. A., 41(6) (2010) 1582-1591.

Journal of Stress Analysis/ Vol. 3, No. 1/ Spring − Summer 2018 43

[11] A. Atrian, S.H. Nourbakhsh, Mechanical behaviorof Al-SiCnp nanocomposite fabricated by hot ex-trusion technique, Int. J. Adv. Des. Manuf. Tech.,11 (2018) 33-41.

[12] S. Sattari, A. Atrian, Effects of the deep rollingprocess on the surface roughness and properties ofan Al-3 vol% SiC nanoparticle nanocomposite fab-ricated by mechanical milling and hot extrusion,Intl J. Min., Met. Mater., 24(7) (2017) 814-825.

[13] K. Rahmani, G.H. Majzoobi, A. Atrian, Anovel approach for dynamic compaction of Mg–SiCnanocomposite powder using a modified Split Hop-kinson Pressure Bar, Powder. Metall., 61(2) (2018)164-177.

[14] G.H. Majzoobi, K. Rahmani, A. Atrian, Temper-ature effect on mechanical and tribological char-acterization of Mg-SiC nanocomposite fabricatedby high rate compaction, Mater. Res. Exp., 5(1)(2018) 015046.

[15] P. Hernández, H. Dorantes, F. Hernandez, R.Esquivel, D. Rivas, V. Lopez, Synthesis and mi-crostructural characterization of Al–Ni3Al com-posites fabricated by press-sintering and shock-compaction, Adv. Powder. Technol., 25(1) (2014)255-260.

[16] W.H. Gourdin, Dynamic consolidation of metalpowders, Prog. Mater Sci., 30(1) (1986) 39-80.

[17] S.K. Thakur, G.T. Kwee, M. Gupta, Developmentand characterization of magnesium composites con-taining nano-sized silicon carbide and carbon nan-otubes as hybrid reinforcements, J. Mater. Sci.,42(24) (2007) 10040-10046.

[18] E.D. Francis, N. Eswara Parsad, Ch. Ratnam,S.K. Pitta, V.K. Venkata, Synthesis of nano alu-mina reinforced magnesium-alloy composites, Int.J. Adv. Sci. Tech., 27 (2011) 35-44.

[19] Q. Jiang, H.Y. Wang, B.X. Ma, Y. Wang, F. Zhao,Fabrication of B4C particulate reinforced magne-sium matrix composite by powder metallurgy, J.Alloy. Compd., 386(1) (2005) 177-181.

[20] J.Z. Wang, X.H. Qu, H.Q. Yin, M.J. Yi, X.J.Yuan, High velocity compaction of ferrous powder,Powder. Technol., 192(1-2) (2009) 131-136.

[21] Z. Yan, F. Chen, Y. Cai, High-velocity compactionof titanium powder and process characterization,Powder. Technol., 208(3) (2011) 596-599.

[22] A.N. Faruqui, Mechanical milling and synthesis ofMg-SiC composites using underwater shock consol-idation, Met. Mater. Int., 18(1) (2012) 157-163.

[23] A. Atrian, G.H. Majzoobi, H. Bakhtiari, M.H.Enayati, A comparative study on hot dynamic com-paction and quasi-static hot pressing of Al7075/SiCnp nanocomposite, Adv. Powder. Technol., 26(1)(2015) 73-82.

[24] G.H. Majzoobi, A. Atrian, M.K. Pipelzadeh, Ef-fect of densification rate on consolidation and prop-erties of Al7075–B4C composite powder, PowderMetall., 58(4) (2015) 281-288.

[25] A. Atrian, G.H. Majzoobi, S.H. Nourbakhsh, S.A.Galehdari, R.M. Masoudi Nejad, Evaluation of ten-sile strength of Al7075-SiC nanocomposite com-pacted by gas gun using spherical indentation testand neural networks, Adv. Powder. Technol., 27(4)(2016) 1821-1827.

[26] A. Mondal, S. Kumar, Dry sliding wear behaviourof magnesium alloy based hybrid composites in thelongitudinal direction, Wear, 267(1-4) (2009) 458-466.

[27] G. Majzoobi, A. Atrian, M. Enayati, Tribologicalproperties of Al7075-SiC nanocomposite preparedby hot dynamic compaction, Compos. Interface.,22(7) (2015) 579-593.

[28] G. Majzoobi, H. Bakhtiari, A. Atrian, Warm dy-namic compaction of Al6061/SiC nanocompositepowders, Proc. Ins. Mech. Eng. L. J. Materi. Des.Appl., 230(2) (2016) 375-387.

[29] Standard, A., E384 (2010e2): Standard testmethod for Knoop and Vickers hardness of materi-als. ASTM Standards, ASTM International, WestConshohocken, PA, (2010).

[30] Standard, A., G99-05, Standard Test Methodfor Wear Testing with a Pin-on-Disk Apparatus,ASTM International, West Conshohocken, PA,(2010).

[31] A. Alizadeh, E. Taheri-Nassaj, Wear behaviorof nanostructured Al and Al-B4C nanocompositesproduced by mechanical milling and hot extrusion,Tribol. Lett., 44(1) (2011) 59.

[32] S. Seetharaman, J. Subramanian, K.S. Tun,A.M.S. Hamouda, M. Gupta, Synthesis and char-acterization of nano boron nitride reinforced mag-nesium composites produced by the microwave sin-tering method. Materials, 6(5) (2013) 1940-1955.

[33] Q. Jiang, H. Wang, J.G. Wang, C.L. Xu, Fab-rication of TiCp/Mg composites by the thermalexplosion synthesis reaction in molten magnesium,Mater. Lett., 57(16-17) (2003) 2580-2583.

An Experimental Investigation into Wear Resistance of Mg-SiC Nanocomposite Produced at High Rate ofCompaction: 35–45 44

[34] M.J. Yi, H.Q. Yin, J.Z. Wang, X.J. Yuan, Com-parative research on high-velocity compaction andconventional rigid die compaction, Front. Mater.Sci. China., 3(4) (2009) 447-451.

[35] Z.B. Wang, N.R. Tao, S. Li, W. Wang, G. Liu, J.Lu, Effect of surface nanocrystallization on frictionand wear properties in low carbon steel, Mater. Sci.Eng. A., 352(1-2) (2003) 144-149.

[36] B. Selvam, P. Marimuthu, R. Narayanasamy, M.Kamaraj, Dry sliding wear behaviour of zinc ox-ide reinforced magnesium matrix nano-composites.Mater. Des., 58 (2014) 475-481.

[37] J. Archard, Contact and rubbing of flat surfaces,J. Appl. Physic., 24(8) (1953) 981-988.

[38] M. Shanthi, Q. Nguyen, M. Gupta, Sliding wearbehaviour of calcium containing AZ31B/Al2O3nanocomposites, Wear, 269(5) (2010) 473-479.

[39] I. Aatthisugan, A.R. Rose, D.S. Jebadurai, Me-chanical and wear behaviour of AZ91D magnesiummatrix hybrid composite reinforced with boroncarbide and graphite, J. Magnesium Alloys, 5(1)(2017) 20-25.

[40] X. Yao, Z. Zhang, Y.F. Zheng, C. Kong, M.Z.Quadir, J.M. Liang, Y.H. Chen, P. Munroe, D.L.Zhang, Effects of SiC nanoparticle content on themicrostructure and tensile mechanical properties

of ultrafine grained AA6063-SiCnp nanocompos-ites fabricated by powder metallurgy, J. Mater.Sci. Technol., 33(9) (2017) 1023-1030.

[41] D. Markov, D. Kelly, Mechanisms of adhesion-initiated catastrophic wear: pure sliding, Wear,239(2) (2000) 189-210.

[42] M. Jafari, M.H. Enayati, M.H. Abbasi, F.Karimzadeh, Compressive and wear behaviors ofbulk nanostructured Al2024 alloy, Mater. Des.,31(2) (2010) 663-669.

[43] S.R. Anvari, F. Karimzadeh, M.H. Enayati, Anovel route for development of Al-Cr-O surfacenano-composite by friction stir processing, J. Al-loy. Compd., 562(Supplement C) (2013) 48-55.

[44] E.M. Sharifi, F. Karimzadeh, M. Enayati, Fabri-cation and evaluation of mechanical and tribologi-cal properties of boron carbide reinforced aluminummatrix nanocomposites, Mater. Des., 32(6) (2011)3263-3271.

[45] Z. Han, L. Lu, K. Lu, Dry sliding tribologicalbehavior of nanocrystalline and conventional poly-crystalline copper, Tribol. Lett., 21(1) (2006) 45-50.

[46] X.R. Lv, S.G. Wang, Y. Liu, K. Long, S. Li, Z.D.Zhang, Effect of nanocrystallization on tribologi-cal behaviors of ingot iron, Wear, 264(7-8) (2008)535-541.

Journal of Stress Analysis/ Vol. 3, No. 1/ Spring − Summer 2018 45

The Prediction of Weld Line Movement in Deep Drawing of Tailor Welded Blanks S. Abdolazimzadeh, S. Mazdak, E. Sharifi, M.R. SheykholeslamiEvaluation of Bond Strength of Reinforcement in Concrete Containing Fibers, Micro-silica and Nano-silica A. Madadi, H. Eskandari-Naddaf, M. Nemati-NejadThe Role of Wheel Alignment Over the Fatigue Damage Accumulation in Vehicle Steering Knuckle K. Reza Kashyzadeh, G.H. Farrahi, M. Shariyat, M.T. AhmadianAn Experimental Investigation into Wear Resistance of Mg-SiC Nanocomposite Produced at High Rate of Compaction G.H. Majzoobi, K. Rahmani, A. AtrianFormation of Micro Shear Bands During Severe Plastic Deformation of BCC Alloys M.H. Farshidi, H. Doryo, M. Yuasa, H. MiyamotoExperimental and Numerical Investigations of Hydromechanical Deep Drawing of a Bilayer Conical Cup M. Molaei, M. Safari, H.D. Azodi, J.Sh. KaramiEffect of Sheet Thickness on Fatigue Behavior of Friction Stir Spot Weld of Al 6061-T6 Lap-shear Configuration A.R. Shahani, A. FarrahiThe Effects of Geometric Parameters Under Small and Large Deformations on Dissipative Performance of Shape Memory Alloy Helical Springs Y. Mohammad Hashemi, M. KadkhodaeiSpan Length Effects on the Progressive Collapse Behaviour in Concrete Structures M. Esmaeilnia Omran, A. Hoseini KaraniEffect of Interlaminar Weak Bonding and Constant Magnetic Field on the Hygrothermal Stresses of a FG Hybrid Cylindrical Shell Using DQM M. SaadatfarModal Numerical Analysis of Helicopter Rotor Sample Using Holzer-Myklestad Method H. Rabiei, S.A. Galehdari